A cathode of a solid-oxide fuel cell includes a first ionic conducting layer, a second layer deposited over the first layer and formed from a mixed ionic and electronic conductor layer including an oxygen ion conducting phase, and a third layer deposited over the second layer and formed from a mixed ionic and electronic conductor layer. A sintering aid and pore formers are added to the second layer and the third layer to establish ionic, electronic, and gas diffusion paths that are contiguous. By adjusting the microstructure of the second and the third layer, a high performance low resistance cathode is formed that bonds well to the electrolyte, is highly electro-catalytic, and has a relatively low overall resistance. By using inexpensive and readily available substances as sintering aid and as pore formers, a low-cost cathode is provided.
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1. A cathode of a solid-oxide fuel cell, comprising:
a first ionic conducting layer comprising ceria;
a second layer deposited over said first layer;
a third layer deposited over said second layer;
a sintering aid comprising caco3 added to said second layer and to said third layer; and
pore formers added to said second layer and to said third layer, wherein said pore formers are selected from a group comprising carbon black, starch, graphite, and non-soluble organics;
wherein said cathode is sintered between about 1000° C. to about 1100° C. such that said sintering aid and said pore formers establish ionic, electronic, and gas diffusion paths.
2. The cathode of
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The present invention was supported in part by a U.S. Government Contract, No. DE-FC26-02NT41246. The United States Government may have rights in the present invention.
The present invention relates to fuel cells; more particularly, to fuel cells having a solid-oxide electrolyte layer separating an anode layer from a cathode layer; and most particularly, to a high performance low resistance three layer cathode and to a method for low-temperature bonding of refractory ceramic layers.
Fuel cells, which generate electric current by the electrochemical combination of hydrogen and oxygen, are well known. In one form of such a fuel cell, an anodic layer and a cathodic layer are separated by an electrolyte formed of a ceramic solid oxide. Such a fuel cell is known in the art as a Solid-Oxide Fuel Cell (SOFC). SOFC systems derive electrical power through a high-efficiency conversion process from a variety of fuels including natural gas, liquefied petroleum gas, ethanol, and other hydrocarbon and non-hydrocarbon fuels. Hydrogen, either pure or reformed from hydrocarbons, is flowed along the outer surface of the anode and diffuses into the anode. Oxygen, typically from air, is flowed along the outer surface of the cathode and diffuses into the cathode.
Each O2 molecule is split and reduced to two O−2 anions catalytically at the cathode/electrolyte interface. The oxygen anions diffuse through the electrolyte and combine with four hydrogen ions at the anode/electrolyte interface to form two molecules of water. The anode and the cathode are connected externally through a load to complete the circuit whereby electrons are transferred from the anode to the cathode.
When hydrogen as a feed stock for the fuel cell is derived by “reforming” hydrocarbons, such as from gasoline, diesel fuel, natural gas, or methane, in the presence of limited oxygen, the reformate gas produced includes CO which is converted to CO2 at the anode/electrolyte interface. Since a single fuel cell is capable of generating a relatively small amount of voltage and wattage, in practice, it is known to stack a plurality of fuel cells together in electrical series.
Present anode supported SOFC technology uses a dense ceramic solid electrolyte membrane, for example yttria stabilized zirconia (YSZ), over which a cathode electrode consisting of an ionic conducting layer and a porous catalyst, such as a mixed ionic and electronic conductor (MIEC), is deposited. The cathode material is predominantly an electronic conductor with some ionic conductivity. At the cathode, oxygen is reduced and the ionic species pass through the electrolyte membrane to the anode where a fuel is oxidized to produce power. The resistance of the cathode, ohmic and polarization, plays a major role in the overall cell resistance and, therefore, can greatly affect electrochemical performance of the cell.
One prior art approach to decrease the cathode resistance (polarization) is to add a doped (Sm, Gd, Nd, Y, etc.) ceria based ionic conducting phase to the mixed ionic and electronic conductor (MIEC) material. While such cathodes may have an initially lower polarization resistance, the polarization resistance increases at elevated cell temperatures as low as about 800° C. In addition, such cathodes are structurally weak and tend to delaminate under certain conditions.
Another prior art approach is to modify the geometry of the cathode to a three layer configuration that includes an ionic conductor layer, a dual phase layer including the mixed ionic and electronic conductor (MIEC) material and ionic conducting material, and a mixed ionic and electronic conductor (MIEC) layer. Such a fuel cell is still susceptible to delamination and the power performance is not improved.
Therefore, cathodes of current solid oxide fuel cells have a high resistance (ohmic and polarization) and, thus, a relatively low power output due to poor adhesion, low ionic conductivity, and an insufficient microstructure of the cathode. Poor adhesion may result in the delamination of the cathode from the electrolyte surface, which may lead to a drastic reduction in output power and even cell failure.
What is needed in the art is a cathode of a solid oxide fuel cell with improved bonding to the electrolyte, that is highly electrocatalytic, and that is porous with contiguous electronic, ionic, and gas diffusion paths.
It is a principal object of the present invention to provide a cathode for a solid-oxide fuel cell that enables significant improvement of the power density of such fuel cell and that has an improved durability.
It is a further object of the invention to provide a method for low-temperature bonding of refractory ceramic layers.
Briefly described, a cathode for a solid oxide fuel cell has a three layer structure that overcomes the low adhesion, the high resistance, the low catalytic activity, and the microstructure related shortcomings of known prior art cathodes.
In one aspect of the invention, the adhesion of the cathode to the electrolyte surface is improved by adding a sintering aid to a center layer that is formed from a mixed ionic and electronic conductor (MIEC) material with an added ionic conducting phase and to a top layer that is formed from a mixed ionic and electronic conductor (MIEC) material. The sintering aid is preferably an alkaline earth metal ion from the group IIA of the periodic table.
In addition, pore formers may be added to the center and the top layer to control the microstructures and porosity of these layers. The combined effect of the sintering aid and the pore formers yields a microstructure that has a relatively low tortuosity. Pore formers are materials such as carbon black, starch, graphite, and the like, non-soluble organics, and other appropriate materials that decompose to leave the desired porosity in the sintered layer.
The overall resistance of the cathode in accordance with the invention is further reduced by including an oxygen ion conducting phase in the composition of the center layer. For this purpose, a mechanical mixture of an ionic conducting phase, for example samaria doped ceria (SDC), and a mixed ionic and electronic conductor, for example lanthanum strontium cobaltite ferrite (LSCF) is prepared. Alternatively, a more homogeneous mixture can be prepared via liquid phases using soluble salts or through solid-state sintering and milling.
Similarly, the composition of the mixed ionic and electronic conductor (MIEC) material, such as LSCF, of the top layer may be varied in terms of relative amounts of its constituents while maintaining a pervoskite structure. The LSCF material may be deficient in A-sites or even a mixture of the two-phase pervoskite structures arising from a large deficiency in A-sites in the crystal structure.
In another aspect of the invention, relatively low sintering temperatures are applied to avoid the formation of resistive phases at the electrode/electrolyte surfaces, to maximize population of active sites by avoiding excessive grain growth, and to maintain high catalytic activity while creating continuous ionic, electronic, and gas diffusion paths that are facile.
The present invention will now be described, by way of example, with reference to the accompanying drawings, in which:
Corresponding reference characters indicate corresponding parts throughout the several views. The exemplification set out herein illustrates one preferred embodiment of the invention, in one form, and such exemplification is not to be construed as limiting the scope of the invention in any manner.
The advantages and benefits afforded to an anode supported solid-oxide fuel cell with a three-layer cathode in accordance with the invention may be better appreciated by first considering prior art anode supported solid-oxide fuel cells. Such fuel cells generate electric current by electrochemical combination of hydrogen and oxygen and include an anode electrode and a cathode electrode separated by an electrolyte formed of a ceramic solid oxide.
Referring to
Referring to
Referring to
As shown in
Referring to
Cathode 430 includes an ionic conducting layer 432, a layer 434 deposited over layer 432 where a doped ceria based ionic conducting phase is added to MIEC material, such as LSCF, and a MIEC layer 436 deposited over layer 434. Ionic conducting layer 432 may be ceria based and doped with, for example samarium (Sm), Gadolinium (Gd), neodymium (Nd), or yttrium (Y).
Adhesion of cathode 430 in accordance with the invention is improved compared to prior art cathode 330 by modifying layers 434 and 436 with a sintering aid 440. The sintering aid 440 is preferably an alkaline earth metal ion from group IIA of the periodic table, such as magnesium (Mg), calcium (Ca), strontium (Sr), and barium (Ba). For example, CaCO3 and MgCO3 or their mixtures have been found to aid in the formation of porous films, are readily available and inexpensive. Other compounds of the alkaline earth metals can be used including aqueous soluble, such as acetates and nitrates, and organic soluble metal-organic compounds to these metals. The amount of the sintering aid 440 contained in the layers 434 and 436 may vary from about 0 wt % (weight percent) to about 10 wt % of solids in the composition, with about 2 wt % to about 6 wt % being the preferred range.
In addition to adding a sintering aid 440, the microstructures of layer 434 and of layer 436 may be controlled by including pore formers 450 in their respective compositions. The purpose of pore formers 450 is to enable the formation of low resistance gas diffusion paths. Pore formers 450 are materials that decompose to leave the desired porosity in the sintered layer, such as layers 434 and 436. For example, carbon black, starch, graphite, and non-soluble organics may be used as pore formers 450. The amount of pore formers 450 may vary from about 0 wt % to about 100 wt % of the solid phase or even higher, with about 10 wt % to about 50 wt % being the preferred range. The constraint on the amount of pore former 450 is the mechanical strength of the resulting films. The combined effect of sintering aid 440 and pore formers 450 yields a microstructure of layers 434 and 436 that has a low tortuosity. The low tortuosity results from rounding of the pores in the porous layers 434 and 436 caused by sintering aid 440 and pore formers 450. By varying the amount of sintering aid 440 and pore formers 450 added to the layers 434 and 436 a desired and application specific microstructure of each of these layers can be achieved without undue experimentation.
In another aspect of the invention, the resistance of cathode 430 is further reduced, compared to prior art cathodes 130, 230, and 330 as illustrated in
In still another aspect of the invention, the composition of the MIEC layer 436 material, for example LSCF, may be varied in terms of relative amounts of its constituents while a pervoskite structure is maintained. The LSCF material of layer 436 may be, for example, deficient in A-sites or may be even a mixture of the two-phase pervoskite structures arising from a relatively large deficiency in A-sites in the crystal structure of layer 436. Other materials that are predominantly electronic conductors, for example LNF, LSC, LSF, LSM, etc. and their combinations, may be used to form MIEC layer 436 instead of LSCF.
Still referring to
Referring to
Graph 500 illustrates electrochemical test results of a variety of test fuel cells 400 that were prepared to demonstrate the performance improvements due to the three layer structure of cathode 430 as described above with
The amounts of CaCO3 as sintering aid 440 and carbon black as pore-former 450 in layers 434 and 436 as well as the amount of the oxygen ion conducting phase 460 in layer 434 were varied to optimize the microstructure of layers 434 and 436. After sintering at temperatures near 1050° C., the total thicknesses of cathode 430 is about 40 μm. One of the advantages of the three layer structure of the cathode 430 in accordance with the invention is that the thickness of cathode 430 could vary over a wide range (>10 μm<100 μm) and still show favorable electrochemical and structural performance as well as structural stability.
As illustrated in
Furthermore, tape pull tests after exposing the test fuel cells 400 to an argon test atmosphere at 1000° C. have shown that the cathodes 430 do not delaminate from the surface of electrolytes 420 contrary to the cathodes 130 of the prior art fuel cells 100.
As can be seen in
While the invention has been described by reference to various specific embodiments, it should be understood that numerous changes may be made within the spirit and scope of the inventive concepts described. Accordingly, it is intended that the invention not be limited to the described embodiments, but will have full scope defined by the language of the following claims.
Thompson, David A., Kerr, Rick D., Jain, Kailash C., Parsian, Mohammad, Keller, Joseph M., Gillispie, Bryan
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